CN103917682B - The high tensile hot rolled steel sheet of flexural property and excellent in low temperature toughness and manufacture method thereof - Google Patents

The high tensile hot rolled steel sheet of flexural property and excellent in low temperature toughness and manufacture method thereof Download PDF

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CN103917682B
CN103917682B CN201280054316.8A CN201280054316A CN103917682B CN 103917682 B CN103917682 B CN 103917682B CN 201280054316 A CN201280054316 A CN 201280054316A CN 103917682 B CN103917682 B CN 103917682B
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hot rolled
rolled steel
temperature
high tensile
cooling
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CN103917682A (en
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上力
山崎和彦
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JFE Engineering Corp
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NKK Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

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  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The present invention provides the high tensile hot rolled steel sheet of a kind of structure member being suitable as heavy construction/industrial machinery.nullC:0.08～0.25% will be consisted of、Si:0.01～1.0%、Mn:0.8～2.1% and P、S、Al adjusts to the former material of steel of proper range the temperature being heated to 1100～1250 DEG C，Carry out roughing，And the accumulation rolling rate in partial, re-crystallization γ region and non-recrystallization γ region that is implemented in is divided by the finish rolling that value obtained from the accumulation rolling rate in recrystallization γ region is 0～0.2，After finish rolling terminates，Immediately begin to cooling，Cool down with the average cooling rate within the temperature range of 750 DEG C～500 DEG C for the cooling velocity generating more than the critical cooling rate of martensite，Within after beginning to cool down 30 seconds，The cooling being cooled to Ms point less than+150 DEG C stops temperature，Keep 5～60 seconds within the temperature range of this cooling stops temperature ± 100 DEG C，And it is taken as web-like at the described coiling temperature last volume cooling down stopping temperature ± 100 DEG C scope.Thus, define and there is the tissue that the average grain diameter that the average grain diameter of the former γ crystal grain as principal phase and in the cross section parallel with rolling direction with tempered martensite phase or low temperature phase change bainite is less than 20 μm and former γ crystal grain in the cross section orthogonal with rolling direction is less than 15 μm, and have the hot rolled steel plate of the high intensity that yield strength YS is more than 960MPa and high tenacity and excellent flexural property concurrently.

Description

The high tensile hot rolled steel sheet of flexural property and excellent in low temperature toughness and manufacture method thereof
Technical field
The present invention relates to be suitable as machinery for building, the structure member of industrial machine (hereinafter also referred to as building/work The structure member of industry machinery) high tensile hot rolled steel sheet, and particularly to the raising of flexural property and low-temperature flexibility.In addition, this Locate so-called " steel plate " and include steel plate, steel band.Additionally, so-called " high tensile hot rolled steel sheet " herein refer to have yield strength The hot rolled steel plate of the high intensity of YS:960～1200MPa level.
Background technology
In recent years, with the high stratification of building, also exist with machinery for construction such as the crane of building constructions thing, trucies Maximize.Additionally, industrial machine also has the trend of maximization.Therefore, it is necessary to mitigate the deadweight of these machineries, it is desirable to make apparatus There is the sheet metal of high intensity of more than yield strength YS:960MPa as the structure member of these heavy construction/industrial machineries.
For this requirement, for example, patent document 1 proposes a kind of processability and the good high strength rolled steel of weldability The manufacture method of plate, wherein by heating steel billet to more than 1250 DEG C, at Ar3 transformation temperature～950 DEG C with more than 80% total eventually The rate of rolling carries out hot rolling, and the cooling velocity with 800～500 DEG C of scopes is 30～80 DEG C/sec and cools down, and at 500 DEG C with last volume Take, wherein said steel billet in terms of quality % containing C:0.05～0.15%, below Si:1.50%, Mn:0.70～2.50%, Ni: 0.25～1.5%, Ti:0.12～0.30%, B:0.0005～0.0015%, and further P, S, Al, N are adjusted to suitable Amount.Technology according to described in patent document 1, can positively manufacture yield point, more than the 950MPa with more than 890MPa The bendability of tensile strength, the high tensile hot rolled steel sheet of excellent weldability.
Additionally, patent document 2 proposes a kind of programming rate with more than 150 DEG C/h, by steel billet from least 1100 It DEG C is heated to the temperature range of the heating-up temperature of more than the melt temperature of TiC and less than 1400 DEG C, and at the heating temperature Retention time be 5～30 minutes, then carry out the manufacture method of the high tensile hot rolled steel sheet of hot rolling, wherein said steel billet is with matter Amount % meter containing C:0.05～0.20%, below Si:0.60%, Mn:0.10～2.50%, solAl:0.004～0.10%, Ti:0.04～0.30%, B:0.0005～0.0015%.In the technology described in patent document 2, utilize the Ti conduct of trace The solid solution B of precipitation-hardening element and trace, as austenite (γ) stabilizing element, makes phase transition temperature during cooling reduce, makes Ferritic structure miniaturization after phase transformation, such that it is able to obtain having the high intensity that tensile strength is about 1020MPa and section The hot rolled steel plate of the high tenacity that transition temperature vTrs is about-70 DEG C.
Additionally, patent document 3 proposes the manufacture of the high tensile hot rolled steel sheet of a kind of bendability, excellent weldability Method, wherein by heating steel billet to more than 1250 DEG C, with total finish to gauge rate 80% heat carried out above at Ar3 transformation temperature～950 DEG C Roll, then cool down less than the cooling velocity of 30 DEG C/sec with 20 DEG C/sec the scope of 800～200 DEG C, 200 DEG C with Under batch, apply the processing strain of 0.2～5.0%, and implement at a temperature of 100～400 DEG C of scopes to keep appropriate time Processing and heat treatment, wherein said steel billet in terms of quality % containing C:0.05～0.15%, below Si:1.50%, Mn:0.70～ 2.50%th, Ni:0.25～1.5%, Ti:0.12～0.30%, B:0.0005～0.0015%, and further P, S, Al, N are adjusted Whole for appropriate amount.Technology according to described in patent document 3, can be easily manufactured yield point and be more than 890MPa, stretch by force The high tensile hot rolled steel sheet that degree is more than 950MPa.
Additionally, patent document 4 has been recorded the manufacture method of the ultrahigh strength hot-rolled steel plate of a kind of excellent processability, wherein It after steel billet is cast, is immediately heated and is again heated to 1100～1300 DEG C to 1100～1300 DEG C or temporarily cooling, then Rolling end temp 950～800 DEG C at carry out hot rolling, begin to cool down within 0.5 second after the end of rolling, with 30 DEG C/sec with On cooling velocity cool down, then batch at 500～300 DEG C, the composition of wherein said steel billet contain C:0.05～ 0.20%th, Si:0.05～0.50%, Mn:1.0～3.5%, below P:0.05%, below S:0.01%, Nb:0.005～ 0.30%th, Ti:0.001～0.100%, Cr:0.01～1.0%, below Al:0.1%, and Si, P, Cr, Ti, Nb, Mn meet Specific relation.Have and be calculated as, with percent by volume, the bayesian that 60% less than 90% thus, it is possible to obtain metal structure Body is principal phase and with the tissue that at least one in pearlite, ferrite, retained austenite, martensite is the 2nd phase, and shellfish The average grain diameter of family name's body phase is less than 4 μm, and tensile strength is more than 980MPa, and stretch flange formability mouldability and strength ductile balance are all Excellent, and also there is the ultrahigh strength hot-rolled steel plate of the excellent processability of low yielding ratio.
Additionally, patent document 5 has been recorded the manufacture method of a kind of high tensile hot rolled steel sheet, wherein by heating steel billet extremely After more than 1000 DEG C, laminated base by roughing, then in finish rolling outlet side temperature: under conditions of more than 800 DEG C, implement essence Roll, then after finish rolling completes within 3 seconds, with average cooling rate: the cooling velocity of more than 20 DEG C/sec is at 400～600 DEG C It in temperature range, is cooled to meet Ta DEG C of 11000-3000 [%V]≤24 × Ta≤15000-1000 [%V], and rolls up Take, the composition of wherein said steel plate contain C:0.10～0.25%, below Si:1.5%, Mn:1.0～3.0%, P:0.10% with Under, below S:0.005%, Al:0.01～0.5%, below N:0.010%, V:0.10～1.0%, and meet (10Mn+V)/ C is more than 50.Thus, it is possible to the volume fraction obtaining having tempered martensite phase is more than 80%, particle diameter: below 20nm contains V Carbide is with 1000/μm3Above amount separates out, and the average grain diameter of the carbide containing V of this particle diameter: below 20nm is 10nm Following tissue, tensile strength is more than 980MPa, strength-ductility balanced excellent high tensile hot rolled steel sheet.
Prior art literature
Patent document
Patent document 1: Japanese Unexamined Patent Publication 05-230529 publication
Patent document 2: Japanese Unexamined Patent Publication 05-345917 publication
Patent document 3: Japanese Unexamined Patent Publication 07-138638 publication
Patent document 4: Japanese Unexamined Patent Publication 2000-282175 publication
Patent document 5: Japanese Unexamined Patent Publication 2006-183141 publication
Content of the invention
Invent problem to be solved
But, the technology described in patent document 1～5, there are the following problems: is difficult to stably guarantee desired shape Shape, and it is difficult to height that is stable and that be easily manufactured the 960MPa level～1100MPa level having more than yield strength YS:960MPa concurrently Intensity and in the test temperature of Charpy-type test: energy absorption vE at-40 DEG C-40: the hot-rolled steel of the high tenacity of more than 40J Plate.
Present invention aim at solving above-mentioned problem of the prior art, provide and be suitable as heavy construction/industrial machinery High tenacity and the excellent high tensile hot rolled steel sheet of flexural property and manufacture method thereof.So-called " high intensity " referring to is surrendered herein Situation more than intensity YS:960MPa, " high tenacity " refers to have vE-40Feelings for more than 30J, the toughness being preferably more than 40J Condition, " flexural property is excellent " refers to that bending radius is that (3.0 × thickness of slab) below and can bend the situation of 180 degree.Additionally, this Invention target hot rolled steel plate, be thickness of slab be more than 3mm and 12mm hot rolling below steel plate.
For solving the method for problem
The present inventor, in order to reach above-mentioned purpose, has the high intensity of more than yield strength YS:960MPa for impact The toughness of hot rolled steel plate, the various factors of ductility conduct in-depth research.It was found that by being formed with bainite or tempering Martensite is principal phase, and the average grain diameter of original austenite (γ) crystal grain in the cross section parallel with rolling direction be 20 μm with The average grain diameter of the former γ crystal grain down and in the cross section orthogonal with rolling direction is the tissue of less than 15 μm, is possible not only to guarantee There is the high intensity that yield strength YS is more than 960MPa, and may insure that excellent toughness and excellent flexural property.
Furthermore, it was found that in order to maintain more excellent flexural property, be preferably formed as the orthogonal with rolling direction of former γ crystal grain The average length in direction relative to the ratio of the average length of rolling direction be (average length of the rolling direction of former γ crystal grain)/ (average length in the direction orthogonal with rolling direction of former γ crystal grain) is the tissue of less than 10, and is preferably formed as X-ray face Intensity 223}<252>({ 223}<252>orientation is for the ratio of X-ray diffraction intensity of random sample) be less than 5.0 tissue.
And find, in order to obtain above-mentioned tissue, it is important that implement successively to add at material former to the steel with predetermined composition Heat the former material of this steel heating process, to after this heating the former material of steel implement be made up of roughing and finish rolling hot rolling hot-rolled process, Refrigerating work procedure and coiling process and when making hot rolled steel plate combination implement following operation: heating process, be heated to 1100～ The operation of the temperature of 1250 DEG C；Hot-rolled process, is implemented in partial, re-crystallization austenite region and not to the sheet billet of roughing gained The accumulation rolling rate of recrystallization austenite region divided by value obtained from the accumulation rolling rate at recrystallization austenite region be 0～ The rolling of 0.2 is as finish rolling；Refrigerating work procedure, is after finish rolling terminates, and immediately begins to cooling, with the temperature model of 750 DEG C～500 DEG C Average cooling rate in enclosing is for generating the cooling velocity of more than the critical cooling rate of martensite, 30 after beginning to cool down second Within be cooled to the cooling of Ms point less than+150 DEG C and stop temperature, and stop within the temperature range of temperature ± 100 DEG C in this cooling Keep the operation of 5～60 seconds；Coiling process, is at the coiling temperature making coiling temperature be that cooling stops temperature ± 100 DEG C scope Last volume is taken as the operation of web-like.
The present invention, based on above-mentioned opinion, has made further research and has completed.It is to say, the following institute of idea of the invention State.
(1) high tensile hot rolled steel sheet of a kind of flexural property and excellent in low temperature toughness, it is characterised in that there is following group Become: containing C:0.08～0.25%, Si:0.01～1.0%, Mn:0.8～2.1%, below P:0.025%, S in terms of quality %: Less than 0.005%, Al:0.005～0.10%, surplus is made up of Fe and inevitable impurity, and has such as undertissue: with Bainite phase or tempered martensite phase are principal phase, and the average grain diameter of original austenite grain is 20 in the cross section parallel with rolling direction It it is less than 15 μm below μm and in the cross section orthogonal with rolling direction.
(2) high tensile hot rolled steel sheet as described in (1), it is characterised in that described original austenite grain and rolling direction The average length in orthogonal direction relative to the average length of rolling direction ratio be (average length of rolling direction)/(with roll The average length in the orthogonal direction in direction processed) it is less than 10.
(3) high tensile hot rolled steel sheet as described in (1) or (2), it is characterised in that described tissue is X-ray face intensity 223}<252>and be less than 5.0 tissue.
(4) high tensile hot rolled steel sheet as according to any one of (1)～(3), it is characterised in that on the basis of described composition On, in terms of quality %, contain B:0.0001～0.0050% further.
(5) high tensile hot rolled steel sheet as according to any one of (1)～(4), it is characterised in that on the basis of described composition On, in terms of quality %, contain further selected from Nb:0.001～0.05%, Ti:0.001～0.05%, Mo:0.001～ 1.0%th, Cr:0.01～1.0%, V:0.001～0.10%, Cu:0.01～0.50%, in Ni:0.01～0.50% at least A kind of.
(6) high tensile hot rolled steel sheet as according to any one of (1)～(5), it is characterised in that on the basis of described composition On, in terms of quality %, contain Ca:0.0005～0.005% further.
(7) manufacture method of the high tensile hot rolled steel sheet of a kind of flexural property and excellent in low temperature toughness, it is characterised in that To steel, former material is implemented successively to heat the heating process of the former material of this steel, is implemented to be made up of roughing and finish rolling to the former material of steel after this heating The hot-rolled process of hot rolling, refrigerating work procedure and coiling process and when making hot rolled steel plate, consisting of of the former material of described steel: with matter Amount % meter contains C:0.08～0.25%, Si:0.01～1.0%, Mn:0.8～2.1%, below P:0.025%, S:0.005% Below, Al:0.005～0.10%, and surplus is made up of Fe and inevitable impurity, described heating process is heated to 1100 The operation of the temperature of～1250 DEG C, the described roughing in described hot-rolled process will in described heating process heat after described in The former material of steel laminates the rolling of base, and the described finish rolling in described hot-rolled process is to be implemented in partial, re-crystallization to described sheet billet The accumulation rolling rate of austenite region and non-recrystallization austenite region is divided by the accumulation rolling rate at recrystallization austenite region Obtained from value be 0～0.2 rolling,
Described refrigerating work procedure is the operation implementing the following processing: cooling process, after described finish rolling terminates, immediately begins to cold But, with the average cooling rate within the temperature range of 750 DEG C～500 DEG C for generating the cold of more than the critical cooling rate of martensite But speed cools down, and is cooled to (Ms transformation temperature+150 DEG C) cooling below and stops temperature within 30 after starting this cooling second Degree；With holding process, after stopping this cooling process, within the temperature range of described cooling stops temperature ± 100 DEG C, keep 5～60 Second, described coiling process is to be taken as the operation of web-like at the coiling temperature last volume of described (cooling stop temperature ± 100 DEG C) scope.
(8) manufacture method of the high tensile hot rolled steel sheet as described in (7), it is characterised in that on the basis of described composition, In terms of quality %, contain B:0.0001～0.0050% further.
(9) manufacture method of the high tensile hot rolled steel sheet as described in (7) or (8), it is characterised in that at the base of described composition On plinth, in terms of quality %, contain further selected from Nb:0.001～0.05%, Ti:0.001～0.05%, Mo:0.001～ 1.0%th, Cr:0.01～1.0%, V:0.001～0.10%, Cu:0.01～0.50%, in Ni:0.01～0.50% at least A kind of.
(10) manufacture method of the high tensile hot rolled steel sheet as according to any one of (7)～(9), it is characterised in that in institute On the basis of stating composition, in terms of quality %, contain Ca:0.0005～0.005% further.
Invention effect
Have concurrently at the high intensity that yield strength YS is more than 960MPa and-40 DEG C according to the present invention it is possible to stably manufacture Charpy-type test energy absorption be the high tenacity of more than 30J and the excellent hot rolled steel plate of flexural property, send out in the industry Wave significant effect.Additionally, the hot rolled steel plate of the present invention, be thickness of slab be more than 3mm and the hot rolled steel plate of below 12mm left and right, It is suitable as large-scale building with machinery, the structure member of industrial machine, and also have to can aid in significantly to mitigate and build If the effect with machinery, the tare of industrial machine.
Detailed description of the invention
First, limit reason to the composition of hot rolled steel plate of the present invention to illustrate.In addition, unless otherwise specified, then Quality % is only denoted as %.
C:0.08～0.25%
C is the element having and increasing hardness of steel effect, in the present invention in order to ensure desired high intensity, it is necessary to contain More than 0.08%.On the other hand, excessively contain more than 0.25%, then cause weldability to decline, also result under base metal tenacity Fall.Therefore, C is limited to the scope of 0.08～0.25%.Additionally, it is preferred that be 0.10～0.20%.
Si:0.01～1.0%
Si is had by solution strengthening, the raising of quenching degree increases the effect of hardness of steel.When containing more than 0.01%, Can confirm that this effect.On the other hand, contain Si in a large number more than 1.0%, then make C be enriched in γ phase, promote γ phase Stabilisation, causes intensity to decline, and forms the oxide containing Si at weld part, causes weld part quality to decline.Therefore, at this In invention, Si is limited to the scope of 0.01～1.0%.In addition, from the viewpoint of suppression γ phase is formed, more preferably Si is set It is set to less than 0.8%.
Mn:0.8～2.1%
Mn is had the effect increasing armor plate strength by the raising of quenching degree.Additionally, Mn fixes S by forming MnS, from And prevent the cyrystal boundary segregation of S, the crackle of suppression steel billet (the former material of steel).In order to obtain this effect, it is necessary to contain more than 0.8%. On the other hand, containing more than 2.1%, then encourage solidifying segregation during steel billet casting, make Mn enrichment portion remain in steel plate, can increase Add the generation in crack.In order to make this Mn enrichment portion disappear, it is necessary to be heated to the temperature more than 1300 DEG C, implement on an industrial scale This heat treatment is unpractical.Therefore, Mn is limited to the scope of 0.8～2.1%.Additionally, it is preferred that be 0.9～2.0%.This Outward, from the viewpoint of preventing delayed fracture, more preferably Mn is set as less than 1.3%.
Below P:0.025%
P is inevitably included in steel as impurity, but has the effect improving hardness of steel.But, if it exceeds 0.025% and excessive contain, then weldability declines.Therefore, P is limited to less than 0.025%.Additionally, it is preferred that be 0.015% with Under.
Below S:0.005%
S and P is same, is inevitably included in steel as impurity, and if it exceeds 0.005% and excessive contain, then Result in crackle of steel billet, and in hot rolled steel plate, form thick MnS, cause ductility to decline.Therefore, S is limited to Less than 0.005%.Additionally, it is preferred that be less than 0.004%.
Al:0.005～0.10%
Al has been the element of deoxidier effect, in order to obtain this effect, preferably comprises more than 0.005%.On the other hand, Containing more than 0.10%, then damage the spatter property of weld part significantly.Therefore, Al is limited to 0.005～0.10%.In addition, It is preferably less than 0.05%.
Mentioned component is basic composition, on the basis of basic composition, can as required, and containing conduct further can Select B:0.0001～0.0050% of element, and/or Nb:0.001～0.05%, Ti:0.001～0.05%, Mo:0.001～ 1.0%th, Cr:0.01～1.0%, V:0.001～0.10%, Cu:0.01～0.50%, a kind in Ni:0.01～0.50% or Two or more, and/or Ca:0.0005～0.005%.
B:0.0001～0.0050%
B is to be segregated to γ crystal boundary and have, by a small amount of containing, the element significantly improving quenching degree effect, in order to really Protecting desired high intensity, it can contain as desired.In order to obtain this effect, it is desirable to contain more than 0.0001%. On the other hand, even if containing more than 0.0050%, owing to its effect is saturated, the effect matching with content therefore cannot be expected, It is economically disadvantageous.Therefore, containing in the case of, preferably B is limited to the scope of 0.0001～0.0050%.Separately Outward, more preferably 0.0005～0.0030%.
Nb:0.001～0.05%, Ti:0.001～0.05%, Mo:0.001～1.0%, Cr:0.01～1.0%, V: 0.001～0.10%, Cu:0.01～0.50%, one kind or two or more in Ni:0.01～0.50%
Nb, Ti, Mo, Cr, V, Cu, Ni are has the element increasing intensity effect, can select as required containing a kind Or two or more.
Nb:0.001～0.05%
Nb is to have without infringement weldability and to make hot rolling with less content for carbonitride by fine precipitation The effect of steel plate high intensity, and there is the element of the effect of the coarsening of suppression austenite crystal, recrystallization simultaneously, it is thus possible to Enough carry out the rolling of austenite non-recrystallization temperature range in hot finishing.In order to obtain this effect, it is desirable to containing 0.001% with On.On the other hand, excessively contain more than 0.05%, then cause the rolling load in hot finishing to increase, be sometimes difficult to heat Roll.Therefore, containing in the case of, preferably Nb is limited to the scope of 0.001～0.05%.In addition, more preferably 0.005～ 0.04%.
Ti:0.001～0.05%
Ti has makes steel plate high intensity and formation nitride fix N and prevent steel by fine precipitation for carbide The effect of base (the former material of steel) crackle.This effect becomes notable when containing more than 0.001%, but contains more than 0.05%, Then due to precipitation strength, causing yield point significantly to rise, toughness declines.Additionally, the melt of Ti carbonitride, require more than The high-temperature heating of 1250 DEG C, and cause the coarsening of former γ crystal grain, it is difficult to adjust the draw ratio of desired former γ crystal grain.Cause This, containing it is sometimes preferred to be limited to the scope of 0.001～0.05% by Ti.In addition, more preferably 0.005～0.035%.
Mo:0.001～1.0%
Mo is to have the element improving quenching degree and formation carbonitride and making the effect of steel plate high intensity.In order to obtain Obtain this effect, it is desirable to contain more than 0.001%.On the other hand, excessively contain more than 1.0%, then cause weldability to decline.Cause This, containing it is sometimes preferred to be defined to 0.001～1.0% by Mo.In addition, more preferably 0.05～0.8%.
Cr:0.01～1.0%
Cr is to have the element improving quenching degree, increasing the effect of armor plate strength.In order to obtain this effect, it is desirable to contain More than 0.01%.On the other hand, excessively contain more than 1.0%, then cause weldability to decline.Therefore, containing it is sometimes preferred to incite somebody to action Cr is defined to 0.01～1.0%.In addition, more preferably 0.1～0.8%.
V:0.001～0.10%
V be in steel solid solution and contributed to by solution strengthening increase armor plate strength and with carbide, nitride or The form of carbonitride is separated out and is contributed to increasing the element of intensity by precipitation strength.In order to obtain this effect, it is desirable to contain Have more than 0.001%.On the other hand, containing more than 0.10%, then toughness is caused to decline.Therefore, containing it is sometimes preferred to limit V It is scheduled on the scope of 0.001～0.10%.
Cu:0.01～0.50%
Cu be in steel solid solution and contribute to increase intensity, simultaneously also improve corrosion resistance element.In order to obtain this effect Really, it is desirable to contain more than 0.01%.On the other hand, containing more than 0.50%, then the surface texture of steel plate is caused to be deteriorated.Therefore, Containing it is sometimes preferred to Cu is limited to the scope of 0.01～0.50%.
Ni:0.01～0.50%
Ni be in steel solid solution and contribute to increase intensity, simultaneously also improve toughness element.In order to obtain this effect, uncommon Hope and contain more than 0.01%.On the other hand, containing the substantial amounts of Ni more than 0.50%, then the surging of material cost is caused.Therefore, Containing it is sometimes preferred to Ni is limited to the scope of 0.01～0.50%.
Ca:0.0005～0.005%
Ca is to have to fix S with CaS form and make sulfide-based field trash spheroidization, thus controls the work of inclusion morphology With and have the matrix reducing around field trash lattice deformability and reduce hydrogen trap can the element of effect, it can root Contain according to needs.In order to obtain this effect, it is desirable to contain more than 0.0005%, and if containing more than 0.005%, then cause CaO increases, and makes corrosion resistance, toughness decline.Therefore, containing it is sometimes preferred to Ca is limited to the model of 0.0005～0.005% Enclose.In addition, more preferably 0.0005～0.0030%.
Balance of Fe beyond mentioned component and inevitable impurity.In addition, as inevitable impurity, Ke Yiyun Permitted below N:0.005%, below O:0.005%, below Mg:0.003%, below Sn:0.005%.
N inevitably contains in steel, but the containing of excess, then crackle when causing the former material of steel (steel billet) to cast is many Send out.Therefore, it is intended that N is limited to less than 0.005%.In addition, more preferably 0.004%.
Additionally, O in steel presented in various oxides, it is to cause under hot-workability, corrosion resistance, toughness etc. The reason that fall.Therefore, wish in the present invention to be reduced as far as, but less than 0.005% can be allowed.In addition, extreme subtracts Low meeting causes the surging of refining cost, it is desirable to reduce O to less than 0.005%.
Mg and Ca is identically formed oxide, sulfide, has the effect that the thick MnS of suppression is formed, but contains and exceed 0.003%, then cause Mg oxide, Mg sulfide bunch multiple, cause toughness to decline.Therefore, it is intended that reduce extremely Mg Less than 0.003%.
Sn is to be mixed into from waste residue as steelmaking feed etc..Sn is the element being easily segregated to crystal boundary etc., if super Cross 0.005% and contain in a large number, then grain-boundary strength declines, and causes toughness to decline.Therefore, it is intended that by Sn reduce to 0.005% with Under.
Then, the restriction reason of hot rolled steel plate tissue of the present invention is illustrated.
The hot rolled steel plate of the present invention, has an above-mentioned composition, and further with bainite phase or tempered martensite phase or shellfish The mixed phase of family name's body phase and tempered martensite phase is as principal phase.In addition, so-called " bainite " herein, refer to low temperature phase change bayesian Body.Additionally, so-called " principal phase " herein refer to that this is calculated as more than 90% with volume fraction, is preferably the situation of more than 95%.Logical Cross in this, as principal phase, it can be ensured that desired high intensity.In addition, the second phase beyond principal phase is ferritic phase or pearlite Phase.If the tissue percentage of the second phase uprises, then intensity declines, it is impossible to guarantee desired high intensity.Therefore, second with Volume fraction meter is preferably less than 10%.In addition, certainly also there be bainite phase, the tempering horse not constituting principal phase beyond above-mentioned second phase The situation of the tissue that family name's body phase mixes.
Additionally, the hot rolled steel plate of the present invention has such as undertissue: with bainite phase or tempered martensite as principal phase or The tissue that they mix, the average grain diameter at the former γ crystal grain in the cross section parallel with rolling direction is less than 20 μm, and Average grain diameter at the former γ crystal grain in the cross section orthogonal with rolling direction is less than 15 μm.By forming this tissue, can be true Guarantor is in the test temperature of Charpy-type test: energy absorption vE at-40 DEG C-40For more than 30J, thus obtain high tenacity and The excellent hot rolled steel plate of flexural property.If the average grain diameter of former γ crystal grain in L direction cross section more than 20 μm, in C direction cross section The coarsening more than 15 μm, then cannot guarantee above-mentioned toughness.It in addition, the average grain diameter of former γ crystal grain, in L direction cross section is preferably Less than 18 μm, be less than 13 μm in C direction cross section.
It additionally, the hot rolled steel plate of the present invention, is preferably formed as the average length in the direction orthogonal with rolling direction of former γ crystal grain Degree is (average length of the rolling direction of former γ crystal grain)/(former relative to the ratio of the average length of the rolling direction of former γ crystal grain The average length in the direction orthogonal with rolling direction of γ crystal grain) be less than 10 tissue.Thus, flexural property carries further High.(if the average length of the rolling direction of former γ crystal grain)/(average length in the direction orthogonal with rolling direction of former γ crystal grain Degree) more than 10, anisotropy strengthens, then and flexural property declines.Additionally, it is preferred that be less than 7.
In addition, for the average length of former γ crystal grain, make the macrograph that former γ crystal grain exposes and shoots, logical Cross image procossing, measure the length of the rolling direction of former γ crystal grain and the length in the direction orthogonal with rolling direction respectively, then enter Row arithmetic average, obtains each average length.
Additionally, the hot rolled steel plate of the present invention, X-ray face intensity 223}<252>({ 223}<252>orientation is for random examination The ratio of the X-ray diffraction intensity of sample) it is preferably less than 5.0.If 223}<252>and face intensity improve more than 5.0, then by force The anisotropy of degree strengthens, and flexural property declines.It is therefore preferable that by steel plate 223}<252>and face intensity settings be 5.0 with Under.In addition, more preferably less than 4.5.Steel plate 223}<252>and X-ray face intensity be by distance thickness of slab surface 1/4 The position of layer utilizes X-ray to carry out texture parsing (ODF) and obtain.
In addition, so-called " { 223}<252>" herein, refer to resolve the texture being obtained by X-ray carry out BUNGE table Show, in φ 2=45 degree cross section represents, be shown as (φ the 1st, Φ, φ 2)=(the 30.5th, the 43.3rd, 45.0) 223}<252>.Separately Outward, as with 223}<252>of equal value orientation, have 322}<225>, 232}<522>, it is considered to orientation of equal value, it is also possible to note Carry for 223}<252>.Thus, in the present invention 223}<252>include the orientation of equivalence.
Then, the preferable production process of hot rolled steel plate of the present invention is illustrated.
To the steel with above-mentioned composition, former material implements to heat the heating process of the former material of this steel, former to the steel after this heating successively The hot-rolled process of the hot rolling that material enforcement is made up of roughing and finish rolling, refrigerating work procedure and coiling process, make hot rolled plate (steel plate).
In addition, the manufacture method of the former material of steel does not needs to be particularly limited to, but preferably melted by conventional method of smelting such as converters Refine the molten steel of above-mentioned composition, and make the former material of the steel such as steel billet by conventional casting methods such as continuous metal cast process.
First, heating process is implemented to the former material of steel of gained.
In heating process, former for steel material is heated to the temperature of 1100～1250 DEG C.When heating-up temperature is less than 1100 DEG C, Deformation drag is high, and rolling load increases, excessive to the load of roller mill.On the other hand, if heating-up temperature is for more than 1250 DEG C High temperature, then coarse grains, low-temperature flexibility decline, and oxide skin growing amount increase, decrease in yield.Therefore, the former material of steel Heating-up temperature be preferably set to 1100～1250 DEG C.In addition, more preferably less than 1240 DEG C.
Then, implement to heating after the former material of steel carry out roughing and laminate base to this sheet billet implement finish rolling And make the hot-rolled process of hot rolled plate.
As long as former for steel material can be made the sheet billet of desired size shape by roughing, its condition does not limit especially Fixed.Have an impact further, since sheet billet thickness declines measurer to the temperature in finishing mill, therefore preferably consider the temperature in finishing mill Degree slippage, entrance finishing temperature and the difference of finish rolling end temp select sheet billet thickness.Thickness of slab as object of the present invention For the hot rolled steel plate of more than 3mm below 12mm left and right, its sheet billet thickness is preferably set to 30～45mm.
It in finish rolling after roughing, is implemented in partial, re-crystallization austenite region and non-recrystallization austenite to sheet billet The accumulation rolling rate in region is worth (hereinafter also referred to as accumulation divided by obtained from the accumulation rolling rate at recrystallization austenite region Rolling rate) it is the rolling of less than 0.2 (including 0).
If accumulation rolling rate is more than 0.2, then former γ crystal grain extends in the rolling direction, it is impossible to guarantee with rolling direction The average grain diameter of the former γ crystal grain in parallel cross section is less than 20 μm and the former γ crystal grain in the cross section orthogonal with rolling direction Average grain diameter be the tissue of less than 15 μm.Additionally, (average length of the rolling direction of former γ crystal grain)/(former γ crystal grain with The average length in the orthogonal direction of rolling direction) more than 10, and the X-ray face intensity at the position on 1/4 layer of thickness of slab surface of distance 223}<252>more than 5, flexural property and toughness decline.It is therefore preferable that by partial, re-crystallization during finish rolling/non-recrystallization region Accumulation rolling rate ratio is limited to less than 0.2.In addition, more preferably less than 0.15.
In addition, for the as-rolled condition realizing above-mentioned finish rolling, in the compositing range of the former material of the steel using in the present invention, excellent Finish rolling entrance side (beginning) temperature is set as the temperature of 900～1050 DEG C of scopes by choosing, sets finish rolling outlet side (end) temperature It is set to the temperature of 800～950 DEG C of scopes, finish rolling entrance side (beginning) temperature is set with outlet side (end) temperature difference Δ T It is less than 200 DEG C.If Δ T increases more than 200 DEG C, then finish rolling end temp declines, and therefore cannot guarantee desired former γ particle diameter.In addition, the temperature of finish rolling uses surface temperature.
Finish rolling in hot-rolled process, usually tandem rolling, the time between passage is short, including partial, re-crystallization γ region not again Crystallization γ region is to high temperature side displacement, and when sheet thickness, the temperature decline amount in finishing mill easily becomes big.Therefore, In order to meet above-mentioned finish rolling condition more evenly, preferably select suitable sheet billet thickness, optimize the thickness of slab progress control of finish rolling (rolling schedule), and utilize scale breaker, thin plate cooling agent (ス ト リ ッ プ Network ラ Application ト) etc. to adjust in finishing mill Temperature slippage.
After finish rolling terminates, the cooling device by being arranged on hot run table implements refrigerating work procedure immediately.Finish rolling terminates After, from sending finishing stand immediately, begin to cool down within preferably 5 seconds.If the holdup time starting to cooling is elongated, then may be used Can exceed the crash time generating martensite, and γ crystal grain carries out grain growth, tempered martensite phase, the plate of bainite phase Bar block size is uneven.
In refrigerating work procedure, at thickness of slab central part, to generate the cooling velocity of more than the critical cooling rate of martensite, Implement within after beginning to cool down 30 seconds to be cooled to the cooling process that (Ms point+150 DEG C) cooling below stops temperature.In addition, Cooling velocity uses the average cooling rate of 750～500 DEG C of temperature ranges.Ms point uses the value being calculated by following formula.In formula In shown element, the element not contained is calculated as zero.
Ms (DEG C)=486-470C-8Si-33Mn-24Cr-17Ni-15Mo
(content (quality %) of herein, C, Si, Mn, Cr, Ni, Mo: each element)
Additionally, it is desirable that proceed by cooling process when the temperature of thickness of slab central part is more than 750 DEG C.If thickness of slab center The temperature in portion is less than 750 DEG C, then form ferrite (polygonal ferrite) or the pearlite of at high temperature phase transformation, it is impossible to form institute Desired tissue.
Additionally, when cooling velocity is less than the critical cooling rate of generation martensite, it is impossible to guarantee with tempered martensite phase Or bainite phase (low temperature phase change bainite phase) is principal phase or their desired tissues of mixing.In addition, cooling speed The upper limit of degree can determine according to the ability of the cooling device being used, and preferably will not bring the cooling that the plate profile such as warpage deteriorate Speed.Preferred cooling velocity is more than 25 DEG C/sec.In addition, in the compositing range of the former material of steel using in the present invention, raw The critical cooling rate becoming martensite is about about 22 DEG C/sec.
Additionally, when cooling stopping temperature is the temperature exceeding (Ms point+150 DEG C), it is impossible to guarantee with bainite phase (low temperature Phase transformation bainite phase) or tempered martensite phase be principal phase or their desired tissues of mixing.Additionally, it is preferred that cold But stopping temperature is (Ms point-200 DEG C)～(Ms point+100 DEG C).If additionally, from cooling starts to stop temperature to cooling Cool time elongated more than 30 seconds, then the second phase beyond martensitic phase and bainite phase (low temperature phase change bainite phase) The tissue percentage of (ferrite, pearlite) increases, and martensitic traoformation, bainitic transformation as phase transformation at low temperatures cannot Fully carry out, sometimes cannot guarantee desired tissue.
Additionally, in refrigerating work procedure, after stopping above-mentioned cooling process, carry out the temperature (cooling stops temperature ± 100 DEG C) The holding process of 5～60 seconds is kept in the range of degree.By implementing this holding process, martensitic phase, the bainite of generation can be made Phase (low temperature phase change bainite phase) is tempered, and separates out fine cementite in lath.Thus, intensity (yield strength) improves, and And toughness improves.It can also enough prevent from becoming the generation of the thick cementite in hydrogen trap site such that it is able to prevent from postponing to break Split.In addition, when keeping temperature less than (cooling stops temperature-100 DEG C), desired tempering effect sometimes cannot be expected.Separately On the one hand, it if keeping temperature to exceed (cooling stops temperature+100 DEG C), then is tempered effect superfluous, cementite coarsening, sometimes Toughness desired by cannot guaranteeing, delayed fracture resistance.
Additionally, when the retention time that holding is processed is less than 5 seconds, it is impossible to expect sufficiently to keep treatment effect, i.e. wished The tempering effect hoped.On the other hand, if it exceeds 60 seconds, then the tempering effect in coiling process reduces, and productivity ratio declines.
In addition, the concrete grammar processing as holding, the methods such as sensing heating can also be used.Additionally, in (cooling stopping Temperature ± 100 DEG C) within the temperature range of holding, the martensitic traoformation heating on hot run table can also be utilized and with reference to setting The land surface pyrometer putting multiple positions on hot run table is carried out by the water yield or the hydraulic pressure in adjustment water-cooled storehouse.
After refrigerating work procedure terminates, batch under the coiling temperature being then implemented in (cooling stops temperature ± 100 DEG C) scope Coiling process for web-like.
In coiling process, batch the hot rolled steel plate for web-like and bear predetermined tempering.If coiling temperature falls in (cooling Stop temperature ± 100 DEG C) scope outside, then cannot guarantee tempering effect desired in coiling process.
Hereinafter, the present invention is described in detail to be based further on embodiment.
Embodiment
Use the steel billet (the former material of steel) (wall thickness: 230mm) of composition shown in table 1, implement the heating process shown in table 2, hot rolling Operation, after hot rolling terminates, implements to carry out the cooling that the holding shown in the cooling process of condition shown in table 2 and table 2 is processed successively Operation, and the coiling process batching under the coiling temperature shown in table 2, make the hot rolled steel plate (steel of thickness of slab shown in table 2 Band).
Cut test film from the hot rolled steel plate of gained, implement structure observation, tension test, impact test.Test method As described below.
(1) structure observation
Cutting structure observation test film from the hot rolled steel plate of gained, to the cross section parallel with rolling direction, (L cuts in direction Face) and the cross section (C direction cross section) orthogonal with rolling direction be ground, and corrode to exposing former γ crystal boundary, use optical microphotograph Mirror (multiplying power: 500 times) tissues observed.Observation place is the position of thickness of slab direction 1/4t.Additionally, respectively observe in each observation place More than 2 visuals field and take pictures, re-use image analysis apparatus, measure the cross section parallel with rolling direction and orthogonal with rolling direction The particle diameter of each original austenite grain in cross section, carry out arithmetic average, calculate the original austenite in the cross section parallel with rolling direction Average grain diameter DC of the original austenite grain in average grain diameter DL of crystal grain and the cross section orthogonal with rolling direction.
Further, the length of the rolling direction of each original austenite grain and the length in the direction orthogonal with rolling direction are measured, Carry out arithmetic average respectively, then calculate its ratio R (=(average length of the rolling direction of original austenite grain)/(with rolling The average length in the orthogonal direction in direction)).
Additionally, the C direction cross section of tissue abrasion's observation test film, and with nital corrosion, use scanning electricity Sub-microscope (multiplying power: 2000 times) above tissues observed taking pictures at the 3s in the region that distance surface is thickness of slab 1/4 position, then Use image analysis apparatus, measure species, the tissue percentage (volume fraction) of each phase of tissue.
Additionally, the ND direction of the hot rolled steel plate at gained, grinding, to the position on 1/4 layer of thickness of slab surface of distance, cuts X-ray Mensuration test film.Chemical grinding is implemented to the X-ray mensuration test film of gained, after removing processing strain, real by X-ray Execute textile analysis (ODF).BUNGE expression is carried out to the textile analysis result of gained, and in φ 2=45 degree cross section represents, asks Go out to be shown as (φ the 1st, Φ, φ 2)=(the 30.5th, the 43.3rd, 45.0) orientation 223}<252>and X-ray intensity.
(2) tension test
From the precalculated position (web length direction end, the position of width 1/4) of the hot rolled steel plate of gained, with roll The orthogonal direction in direction processed (C direction) is test film (parallel portion width: 25mm, the punctuate that the mode of length direction cuts tabular Spacing: 50mm), and according to the regulation of JISZ2241, at room temperature implement tension test, obtain yield strength YS, stretching by force Degree TS, percentage of total elongation El.
(3) impact test
Thickness of slab from the precalculated position (web length direction end, the position of width 1/4) of the hot rolled steel plate of gained Central part, cuts V notch test piece in the way of the direction (C direction) orthogonal with rolling direction is as length direction, and according to The regulation of JIS Z2242 implements Charpy-type test, obtains in test temperature: energy absorption vE at-40 DEG C-40(J).In addition, Test film is 3, obtains the arithmetic mean of instantaneous value of the energy absorption value of gained, as energy absorption value vE of this steel plate-40 (J).In addition, for the steel plate less than 10mm for the thickness of slab, record the measured value under small size.
(4) bend test
Cut bend test piece (long side is the side at a right angle with rolling direction from the precalculated position of the hot rolled steel plate of gained To and be 300mm and short brink is thickness of slab the rectangle test film of more than 5 times), implement 180 degree of bend tests, obtain not Inside the minimum cracking, bending radius (mm) is as minimum bending radius, and calculates minimum bending radius/thickness of slab.By minimum Bending radius/thickness of slab be less than 3.0 situation be evaluated as " flexural property is excellent ".
Acquired results is shown in table 3.
Example of the present invention has all prepared high intensity and the vE with more than yield strength YS:960MPa-40Height for more than 30J Toughness and there is the minimum bending radius not cracked for the high intensity of (3.0 × thickness of slab) excellent flexural property below Hot rolled steel plate.On the other hand, the comparative example outside the scope of the present invention that falls has obtained yield strength YS and has been less than 960MPa or vE-40 Exceed (3.0 × thickness of slab) less than 30J or the minimum bending radius not cracked, it is impossible to meet desired high intensity and high-ductility Property and the hot rolled steel plate of desired excellent flexural property.

Claims (17)

1. the high tensile hot rolled steel sheet of a flexural property and excellent in low temperature toughness, it is characterised in that
There is following composition: in terms of quality % containing C: greater than 0.10% and less than 0.25%, Si:0.01～1.0%, Mn:0.8 ～2.1%, below P:0.025%, below S:0.005%, Al:0.005～0.10%, surplus is by Fe and inevitable impurity Constitute,
And have such as undertissue: with bainite phase or tempered martensite as principal phase, the average grain diameter of original austenite grain exists The cross section parallel with rolling direction is less than 20 μm and is less than 15 μm in the cross section orthogonal with rolling direction.
2. high tensile hot rolled steel sheet as claimed in claim 1, it is characterised in that described original austenite grain and rolling direction The average length in orthogonal direction relative to the average length of rolling direction ratio be (average length of rolling direction)/(with roll The average length in the orthogonal direction in direction processed) it is less than 10.
3. high tensile hot rolled steel sheet as claimed in claim 1 or 2, it is characterised in that described tissue is X-ray face intensity 223}<252>and be less than 5.0 tissue.
4. high tensile hot rolled steel sheet as claimed in claim 1 or 2, it is characterised in that on the basis of described composition, with matter Amount % meter, contains B:0.0001～0.0050% further.
5. high tensile hot rolled steel sheet as claimed in claim 3, it is characterised in that on the basis of described composition, with quality % Meter, contains B:0.0001～0.0050% further.
6. the high tensile hot rolled steel sheet as according to any one of claim the 1st, the 2nd, 5, it is characterised in that on the basis of described composition On, in terms of quality %, contain further selected from Nb:0.001～0.05%, Ti:0.001～0.05%, Mo:0.001～ 1.0%th, Cr:0.01～1.0%, V:0.001～0.10%, Cu:0.01～0.50%, in Ni:0.01～0.50% at least A kind of.
7. high tensile hot rolled steel sheet as claimed in claim 3, it is characterised in that on the basis of described composition, with quality % Meter, contain further selected from Nb:0.001～0.05%, Ti:0.001～0.05%, Mo:0.001～1.0%, Cr:0.01～ 1.0%th, V:0.001～0.10%, Cu:0.01～0.50%, at least one in Ni:0.01～0.50%.
8. high tensile hot rolled steel sheet as claimed in claim 4, it is characterised in that on the basis of described composition, with quality % Meter, contain further selected from Nb:0.001～0.05%, Ti:0.001～0.05%, Mo:0.001～1.0%, Cr:0.01～ 1.0%th, V:0.001～0.10%, Cu:0.01～0.50%, at least one in Ni:0.01～0.50%.
9. the high tensile hot rolled steel sheet as according to any one of claim the 1st, the 2nd, the 5th, the 7th, 8, it is characterised in that at described composition On the basis of, in terms of quality %, contain Ca:0.0005～0.005% further.
10. high tensile hot rolled steel sheet as claimed in claim 3, it is characterised in that on the basis of described composition, with quality % Meter, contains Ca:0.0005～0.005% further.
11. high tensile hot rolled steel sheets as claimed in claim 4, it is characterised in that on the basis of described composition, with quality % Meter, contains Ca:0.0005～0.005% further.
12. high tensile hot rolled steel sheets as claimed in claim 6, it is characterised in that on the basis of described composition, with quality % Meter, contains Ca:0.0005～0.005% further.
The manufacture method of the high tensile hot rolled steel sheet of 13. 1 kinds of flexural properties and excellent in low temperature toughness, it is characterised in that to steel Former material is implemented to heat the heating process of the former material of this steel, the heat being made up of the steel former material enforcement after this heating roughing and finish rolling successively The hot-rolled process, refrigerating work procedure and the coiling process that roll and when making hot rolled steel plate,
Consisting of of the former material of described steel: in terms of quality % containing C:0.08～0.25%, Si:0.01～1.0%, Mn:0.8～ 2.1%th, below P:0.025%, below S:0.005%, Al:0.005～0.10%, and surplus are by Fe and inevitable impurity Constitute,
Described heating process is heated to the operation of the temperature of 1100～1250 DEG C,
Described roughing in described hot-rolled process is that the former material of described steel after heating in described heating process laminates base Rolling, the described finish rolling in described hot-rolled process is to be implemented in partial, re-crystallization austenite region and not again to described sheet billet The accumulation rolling rate of crystallization austenite region divided by value obtained from the accumulation rolling rate at recrystallization austenite region be 0～ The rolling of 0.2,
Described refrigerating work procedure is the operation implementing the following processing: cooling process, after described finish rolling terminates, immediately begins to cooling, With the average cooling rate within the temperature range of 750 DEG C～500 DEG C for generating the cooling of more than the critical cooling rate of martensite Speed cools down, and is cooled to (Ms transformation temperature+150 DEG C) cooling below and stops temperature within 30 seconds after starting described cooling Degree；With holding process, after stopping this cooling process, within the temperature range of described cooling stops temperature ± 100 DEG C, keep 5～60 Second,
Described coiling process is to be taken as the work of web-like at the coiling temperature last volume of described (cooling stop temperature ± 100 DEG C) scope Sequence.
The manufacture method of 14. high tensile hot rolled steel sheets as claimed in claim 13, it is characterised in that on the basis of described composition On, in terms of quality %, contain B:0.0001～0.0050% further.
The manufacture method of 15. high tensile hot rolled steel sheets as described in claim 13 or 14, it is characterised in that at described composition On the basis of, in terms of quality %, contain further selected from Nb:0.001～0.05%, Ti:0.001～0.05%, Mo:0.001～ 1.0%th, Cr:0.01～1.0%, V:0.001～0.10%, Cu:0.01～0.50%, in Ni:0.01～0.50% at least A kind of.
The manufacture method of 16. high tensile hot rolled steel sheets as described in claim 13 or 14, it is characterised in that at described composition On the basis of, in terms of quality %, contain Ca:0.0005～0.005% further.
The manufacture method of 17. high tensile hot rolled steel sheets as claimed in claim 15, it is characterised in that on the basis of described composition On, in terms of quality %, contain Ca:0.0005～0.005% further.
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Families Citing this family (58)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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RU2605037C1 (en) * 2015-11-20 2016-12-20 Федеральное Государственное Унитарное Предприятие "Центральный научно-исследовательский институт черной металлургии им. И.П. Бардина" (ФГУП "ЦНИИчермет им. И.П. Бардина") Method for production of high-strength hot-rolled steel
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JP6477570B2 (en) * 2016-03-31 2019-03-06 Ｊｆｅスチール株式会社 Hot-rolled steel sheet and manufacturing method thereof
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CN106584012B (en) * 2016-12-30 2019-07-12 常州世竟液态金属有限公司 A kind of amorphous alloy shaping methods
JP6760407B2 (en) * 2017-02-16 2020-09-23 日本製鉄株式会社 Hot-rolled steel sheet and its manufacturing method
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WO2018163189A1 (en) * 2017-03-10 2018-09-13 Tata Steel Limited Hot rolled steel product with ultra-high strength minimum 1100mpa and good elongation 21%
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KR20230075081A (en) * 2021-11-22 2023-05-31 주식회사 포스코 High strength hot rolled steel sheet having shape correction property and method of manufactring the same
CN115821156B (en) * 2022-11-10 2024-04-19 舞阳钢铁有限责任公司 Super-thick S355MLO steel plate for fixing offshore structure and production method thereof
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CN118086782A (en) * 2024-04-28 2024-05-28 江苏永钢集团有限公司 High-plasticity hot-rolled wire rod for 8.8-grade non-adjustable bolt and manufacturing method thereof

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1146784A (en) * 1995-01-26 1997-04-02 新日本制铁株式会社 Weldable high-tensile steel excellent in low-temp. toughness
CN101535518A (en) * 2006-11-02 2009-09-16 Posco公司 Steel plate for linepipe having ultra-high strength and excellent low temperature toughness and manufacturing method of the same
CN101676430A (en) * 2008-09-18 2010-03-24 韩国机械研究院 Weldable super-strength steel with excellent low-temperature flexibility and method for manufacturing the same

Family Cites Families (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0295500B2 (en) * 1987-06-03 2003-09-10 Nippon Steel Corporation Hot rolled steel sheet with a high strength and a distinguished formability
JP2556411B2 (en) 1992-02-25 1996-11-20 新日本製鐵株式会社 Method for producing high-strength hot-rolled steel sheet with good workability and weldability
JP3043517B2 (en) 1992-06-15 2000-05-22 新日本製鐵株式会社 Manufacturing method of high strength hot rolled steel sheet
US5634988A (en) 1993-03-25 1997-06-03 Nippon Steel Corporation High tensile steel having excellent fatigue strength at its weld and weldability and process for producing the same
JPH07138638A (en) 1993-11-16 1995-05-30 Nippon Steel Corp Production of high-strength hot rolled steel sheet having good workability and weldability
JP2000282175A (en) 1999-04-02 2000-10-10 Kawasaki Steel Corp Superhigh strength hot-rolled steel sheet excellent in workability, and its production
US20030015263A1 (en) * 2000-05-26 2003-01-23 Chikara Kami Cold rolled steel sheet and galvanized steel sheet having strain aging hardening property and method for producing the same
US6364968B1 (en) * 2000-06-02 2002-04-02 Kawasaki Steel Corporation High-strength hot-rolled steel sheet having excellent stretch flangeability, and method of producing the same
JP4692015B2 (en) * 2004-03-30 2011-06-01 Ｊｆｅスチール株式会社 High ductility hot-rolled steel sheet with excellent stretch flangeability and fatigue characteristics and method for producing the same
JP4682822B2 (en) 2004-11-30 2011-05-11 Ｊｆｅスチール株式会社 High strength hot rolled steel sheet
JP5068688B2 (en) * 2008-04-24 2012-11-07 新日本製鐵株式会社 Hot-rolled steel sheet with excellent hole expansion
JP5369712B2 (en) * 2009-01-28 2013-12-18 Ｊｆｅスチール株式会社 Hot press member excellent in ductility, steel plate for hot press member, and method for producing hot press member
KR101686257B1 (en) * 2009-01-30 2016-12-13 제이에프이 스틸 가부시키가이샤 Heavy gauge, high tensile strength, hot rolled steel sheet with excellent hic resistance and manufacturing method therefor
JP5609383B2 (en) 2009-08-06 2014-10-22 Ｊｆｅスチール株式会社 High strength hot rolled steel sheet with excellent low temperature toughness and method for producing the same
JP4978741B2 (en) * 2010-05-31 2012-07-18 Ｊｆｅスチール株式会社 High-strength hot-rolled steel sheet excellent in stretch flangeability and fatigue resistance and method for producing the same
US20130095347A1 (en) * 2010-06-14 2013-04-18 Kaoru Kawasaki Hot-stamped steel, method of producing of steel sheet for hot stamping, and method of producing hot-stamped steel
BR112013001864B1 (en) * 2010-07-28 2019-07-02 Nippon Steel & Sumitomo Metal Corporation HOT LAMINATED STEEL SHEET, COLD LAMINATED STEEL SHEET, GALVANIZED STEEL SHEET AND SAME PRODUCTION METHOD
JP5776398B2 (en) * 2011-02-24 2015-09-09 Ｊｆｅスチール株式会社 Low yield ratio high strength hot rolled steel sheet with excellent low temperature toughness and method for producing the same
US9938599B2 (en) * 2011-03-29 2018-04-10 Jfe Steel Corporation Abrasion resistant steel plate or steel sheet excellent in resistance to stress corrosion cracking and method for manufacturing the same
KR101638707B1 (en) * 2011-07-20 2016-07-11 제이에프이 스틸 가부시키가이샤 Low yield ratio and high-strength hot rolled steel sheet with excellent low temperature toughness and method for producing the same

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1146784A (en) * 1995-01-26 1997-04-02 新日本制铁株式会社 Weldable high-tensile steel excellent in low-temp. toughness
CN101535518A (en) * 2006-11-02 2009-09-16 Posco公司 Steel plate for linepipe having ultra-high strength and excellent low temperature toughness and manufacturing method of the same
CN101676430A (en) * 2008-09-18 2010-03-24 韩国机械研究院 Weldable super-strength steel with excellent low-temperature flexibility and method for manufacturing the same

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